EP0764487A1 - Préparation d'ébauches métalliques sans moule - Google Patents

Préparation d'ébauches métalliques sans moule Download PDF

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Publication number
EP0764487A1
EP0764487A1 EP96111522A EP96111522A EP0764487A1 EP 0764487 A1 EP0764487 A1 EP 0764487A1 EP 96111522 A EP96111522 A EP 96111522A EP 96111522 A EP96111522 A EP 96111522A EP 0764487 A1 EP0764487 A1 EP 0764487A1
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EP
European Patent Office
Prior art keywords
powder
preform
support
preform part
polymer binder
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Granted
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EP96111522A
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German (de)
English (en)
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EP0764487B1 (fr
Inventor
Clifford C. Bampton
Robert Burkett
Hong-Son Ryang
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Boeing North American Inc
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Rockwell International Corp
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/09—Mixtures of metallic powders
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/10—Formation of a green body
    • B22F10/16—Formation of a green body by embedding the binder within the powder bed
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/30—Process control
    • B22F10/34—Process control of powder characteristics, e.g. density, oxidation or flowability
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/40—Structures for supporting workpieces or articles during manufacture and removed afterwards
    • B22F10/43—Structures for supporting workpieces or articles during manufacture and removed afterwards characterised by material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y10/00—Processes of additive manufacturing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
    • B33Y40/20—Post-treatment, e.g. curing, coating or polishing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y70/00—Materials specially adapted for additive manufacturing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/30—Process control
    • B22F10/37—Process control of powder bed aspects, e.g. density
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/40—Structures for supporting workpieces or articles during manufacture and removed afterwards
    • B22F10/47—Structures for supporting workpieces or articles during manufacture and removed afterwards characterised by structural features
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F2003/1042—Sintering only with support for articles to be sintered
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2503/00—Use of resin-bonded materials as filler
    • B29K2503/04—Inorganic materials
    • B29K2503/06—Metal powders, metal carbides or the like
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the present invention relates to methods of free form fabrication and, in particular, to a method of free form fabrication of metallic components using selective laser binding and transient liquid sintering of blended powders.
  • a single layer of powder having the base alloy composition of the metallic component such as Haynes 230 superalloy, for example, was spread in a thickness equivalent to 85% of a single layer segment in a two-dimensional laminate component build-up process.
  • a second layer of depressed melting temperature powder such as Haynes 230 alloy with 3% boron by weight, for example, was spread over the first powder layer to a thickness equivalent to the final 15% of the complete layer of the stereo lithographic segment of the component.
  • the powder layers were pre-heated in an inert environment to a temperature just below the melting temperature of the top powder layer.
  • a sufficiently intense laser beam was focused on selected areas of the top layer to melt the top powder.
  • the liquid metal rapidly wicked into the powder layer immediately below and isothermally solidified as the melting temperature depressant (boron, in this example) diffused out of the liquid phase into the solid powder.
  • This process rapidly produced a nearly fully dense segment of the component.
  • Fresh powder layers were then spread on top and the process repeated to progressively build up the complete solid component layer-by-layer according to computer-aided design data.
  • a final hot isostatic pressure (HIP) treatment was used to close the small amount of isolated porosity.
  • a limitation of the foregoing process using conventional equipment is that the temperature of the powder bed cannot be raised easily above about 200°C.
  • the laser beam must raise the temperature of the top layer of powder to above its melting point, typically in excess of 1000°C.
  • the component is subjected to severe temperature gradients that produce residual stresses and distortion of the component as it is being built up.
  • a polymer powder was blended with a metal powder.
  • Selective laser sintering as described above, was then used to melt the polymer powder constituent.
  • the melted polymer bound the metal powder in place, layer-by-layer, to form a solid, but porous object.
  • the component was heated to burn out the polymer binder, it was subjected to partial (solid state) sintering to impart residual strength to the remaining metal powder for subsequent densification.
  • the partially sintered component was then densified by infiltration with a lower melting point liquid metal (such as copper for a steel powder part, for example) or by hot isostatic pressing (HIP), which required some form of encapsulation to transfer the HIP gas pressure to the porous component.
  • a lower melting point liquid metal such as copper for a steel powder part, for example
  • HIP hot isostatic pressing
  • the present invention comprises a method of free form fabrication of metallic components by selective laser sintering (SLS) of blended powders, typically using computer aided design (CAD) data.
  • the blended powder used in the present method comprises a parent or base metal alloy that constitutes approximately 75-85% of the total blend; a lower melting temperature metal powder, typically comprising an alloy of the base metal, that constitutes approximately 5-15% of the total blend; and a polymer binder that constitutes approximately 5-15% of the total blend.
  • the powder blend may be used in a conventional SLS apparatus to build up a preform part, layer-by-layer, by localized laser melting of the polymer constituent of the powder, which rapidly resolidifies to bind the metal particles of the powder with connecting necks or bridges.
  • the polymer constituent comprises a fine, high purity, spherical particle nylon powder.
  • the binder is eliminated in a vacuum furnace at elevated temperature and low atmospheric pressure.
  • the polymer sintered powder morphology of the present process provides open, connected pores for easy flow of the polymer vapor to the surface of the preform part without build up of local pockets of vapor pressure that might damage the part.
  • a supporting powder such as a ceramic powder, for example
  • the support powder comprises fine, spherical grains that flow easily and provide continuous support for all regions of the densifying part to prevent cracking or slumping under gravitational forces.
  • An alternate method of providing support for the preform part is to fabricate preform ("green"; i.e., not densified) support tooling comprising structurally supporting shapes.
  • the green support tooling may be fabricated by SLS at the same time as the preform part by using volumes of the blended powder not needed for the part. If the support tooling requires large volumes of expensive alloy powder, the support tooling can be made in a separate SLS process using less expensive alloy powders.
  • the green support tooling may be sprayed with a fine coating of alumina or yttria powder (for example) to prevent the supporting shapes from adhering to the preform part during the transient liquid sintering densification process.
  • the green tooling which comprises preform material (i.e., not densified) having substantially the same shrink rate as the preform part, may be placed under and around the part as necessary to provide structural support during the densification process.
  • the same vacuum furnace used for binder removal is generally be used for transient liquid sintering and densification of the supported part by controlled heat treatment. Controlled heat up rates and isothermal hold times within a narrow temperature range cause transient liquid sintering of the part to near full density with the desired shape and dimensional tolerances.
  • the maximum isothermal hold temperature for the part is above the melting point of the lower temperature alloy but below the melting point of the base metal alloy.
  • the densified part may be subjected to a hot isostatic pressing (HIP) treatment.
  • HIP treatment may be necessary to close residual porosity and complete the chemical homogenization of the part, particularly with respect to the temperature lowering component of the alloy. Elimination of residual porosity is important to improve fatigue properties of the part, and homogenization of the alloy can improve the properties of ambient temperature ductility, toughness, and high temperature strength.
  • a principal object of the invention is rapid free form fabrication of metallic components.
  • a feature of the invention is selective laser binding and transient liquid sintering of a powder blend containing a base metal, a lower melting temperature metal, and a polymer binder.
  • An advantage of the invention is rapid production of complex shaped metal prototypes and complete small batch production runs of high cost metal components without the need for tooling or machining.
  • the present invention comprises a method of free form fabrication of metallic components by selective laser binding and transient liquid sintering of blended powders.
  • the method which may use computer aided design data directly from a computer processor, has utility for rapid production of complex shaped metal prototypes and for complete small batch production runs of high cost components or dies without the need for special tooling or machining operations.
  • One powder comprises the desired parent or base metal alloy, such as nickel-based Haynes 230 superalloy, as an example, that constitutes approximately 75-85% (preferably about 82%) of the total powder blend.
  • the base metal may be selected from metallic elements, such as nickel, iron, cobalt, copper, tungsten, molybdenum, rhenium, titanium, and aluminum, for example, that can be formed into suitable powders and subsequently densified by a transient liquid sintering process.
  • a second powder which constitutes approximately 5-15% (preferably about 10%) of the total blend, generally comprises the same base metal alloy as the first powder but with a sufficient amount of an alloying element, such as boron (typically about 3-4%), for example, added to lower the melting point of the alloy by at least about 200°C, and preferably by 300-400°C.
  • an alloying element such as boron (typically about 3-4%), for example, added to lower the melting point of the alloy by at least about 200°C, and preferably by 300-400°C.
  • Other alloying elements that may be used as melting point depressants include, for example, silicon, carbon, phosphorus, and a large number of metallic elements that form low melting point eutectic compositions with the various base metals described above (such as magnesium with aluminum, for example).
  • the average particle size of the metal powders is generally in the range of about 1-55 ⁇ m (preferably in the range of about 25-55 ⁇ m), and may be specified as -325 mesh, for example.
  • a third powder, which constitutes approximately 5-15% (preferably about 8%) of the total blend, comprises a polymer binder.
  • the average particle size of the polymer binder powder is generally in the range of 1-50 ⁇ m (preferably in the range of about 3-8 ⁇ m). It should be noted that the present process is applicable to other materials and compositions, and one skilled in the art will understand that the alloys, blend percentages, and temperatures described herein are presented as examples and not limitations of the present invention.
  • FIG. 1 shows a side cross-sectional view of an SLS apparatus 10 and a part 15 undergoing fabrication.
  • SLS apparatus 10 includes side walls 12 and a platform or table 14.
  • Table 14 may be heated with coils 16, for example, embedded in table 14.
  • Table 14 may be constructed to descend incrementally within walls 12 to form a cavity for containing a powder 18 to be sintered.
  • a means 20 may be positioned on apparatus 10 for spreading measured layers of powder 18 atop table 14 within the sintering cavity.
  • Powder 18, which comprises a three-part blend as described above, is used in the present process to build up a preform shape of the desired part 15.
  • Means 20 may be used to spread a thin layer (approximately 0.001" to 0.020", for example) of powder 18 atop table 14, which is initially positioned just below the top of walls 12.
  • Table 14 may be heated with coils 16 to bring the temperature of blended powder 18 to a desired level below the melting point of the polymer binder constituent.
  • a beam 22 from a laser 24 is scanned over the layer of blended powder 18, typically as directed by a computer processor 25 having computer aided design (CAD) data for part 15, to perform selective laser sintering of powder 18.
  • CAD computer aided design
  • beam 22 is provided by a laser in the infrared or near infrared region, although any focused beam of energy that is sufficiently intense to generate precise, localized heating may be used.
  • the SLS process causes localized melting of the polymer constituent of the layer of blended powder 18 as it is scanned by laser beam 22. The melted polymer rapidly resolidifies to bind the metal constituents of powder 18 with connecting necks or bridges between metal particles.
  • table 14 is lowered a predetermined increment, a new layer of powder 18 is spread atop the previous layer, and the SLS process is repeated to build up part 15 layer-by-layer according to the design plan provided by computer processor 25.
  • blended powder 18 An important aspect of the present invention, compared to conventional SLS of 100% polymer powders, is the use of a relatively small volume fraction of polymer binder (about 5-15%, for example) in blended powder 18.
  • the polymer constituent of blended powder 18 comprises a fine, high purity, spherical particle nylon powder having an average particle size in the range of approximately 3-8 ⁇ m.
  • Blended powder 18, formulated as described above, has the following attributes: (1) excellent flow characteristics in SLS apparatus 10; (2) excellent laser sintering characteristics, with less thermal distortion and higher repeatability between builds compared with conventional 100% polymer powders (resulting from higher thermal conductivity of the metal content of blended powder 18); (3) high metal volume fraction in the "green" preform part (i.e., prior to densification) resulting from the low volume fraction of polymer binder, excellent powder flow characteristics, and high tap-density provided by an all-spherical, controlled size distribution powder blend; and (4) high dimensional tolerance, surface finish, and robustness of the polymer bound preform part 15 due to the strong bridging behavior of the liquid polymer binder between metal particles under natural surface tension forces.
  • built-up preform part 15 is removed from SLS apparatus 10. Elimination of the polymer binder constituent from preform part 15 may be achieved by placing part 15 in a vacuum furnace at elevated temperature (about 300-500°C, for example) and low atmospheric pressure.
  • the use of a low volume fraction of the preferred high purity nylon binder has the advantages of (a) very low contamination of the base metal from binder residue (mainly carbon) due to high purity of the initial nylon powder, and (b) relatively rapid outgassing with minimal physical damage to porous preform part 15 due to the low volume fraction of nylon and its preferential location as bridges across metal particle contact points.
  • the polymer sintered powder morphology of the present process provides open, connected pores for easy flow of the nylon vapor to the surface of preform part 15 during the vacuum furnace outgassing process without build up of local pockets of vapor pressure that could damage preform part 15.
  • a support powder may be used to surround preform part 15 during the densification process.
  • suitable support powders for part 15 include ceramic powders, such as yttria, zirconia, silicon nitride, and boron nitride, and metal powders having a ceramic surface coating, such as nickel aluminide (Ni 3 Al) powder with a nitrided surface, for example.
  • the supporting powder comprises fine, spherical grains to flow easily, ensure uniform heating during densification, and provide continuous support for all regions to prevent cracking or slumping of part 15 under gravitational forces.
  • the supporting powder should possess sufficient thermal conductivity to provide uniform heating, be non-reactive with metal part 15, and be non-agglomerating at the temperatures required for the transient liquid sintering process. Non-uniform heating of part 15 can cause cracking due to unequal shrinkage during the densification process. Agglomeration can cause excess support powder to become trapped in cavities and result in stress cracking of densifying part 15.
  • Uniform heat transfer and sustained support for densifying part 15 can be enhanced by providing the support powder in a gently fluidized bed, which can be produced by either a mechanical stirring action or a recirculating gas.
  • a recirculating gas should be selected so as to not hinder (and preferably to enhance) the transient liquid sintering process.
  • a gas mixture of methane, hydrogen, and nitrogen for example, will enhance the sintering rate and increase the hardness of a ferrous or nickel alloy part.
  • An ideal powder for a fluidized medium is a material with a similar or slightly lower density than that of the part to be heat treated in the transient liquid sintering process.
  • a fluidized heat treatment bed for a nickel or steel alloy part for example, can be provided by a nickel aluminide powder that has been treated to provide a thick surface nitride coating on the nickel aluminide powder particles.
  • An alternate method of providing support for preform part 15 is to fabricate preform ("green") support tooling (i.e., structurally supporting shapes), illustrated in Figure 1 as shapes 28.
  • Green support shapes 28 may be fabricated by SLS at the same time as preform part 15 by using volumes of blended powder 18 not needed for part 15. If powder 18 comprises an expensive alloy powder and the support tooling requires large volumes, the support tooling can be made in a separate SLS process using a less expensive alloy powder.
  • the green support shapes 28 may be sprayed with a fine coating of a release agent, such as alumina or yttria powder, for example, to prevent supporting shapes 28 from adhering to preform part 15 during the transient liquid sintering densification process.
  • the green shapes 28, which comprise material having the same shrink rate as the preform part (or substantially the same shrink rate if a less expensive alloy is used), are placed under and around part 15 as necessary to provide structural support during the densification process.
  • the lower melting temperature constituent of the metal powder blend is prealloyed with the base alloy composition so as to melt quickly and uniformly when the liquid phase sintering temperature is exceeded.
  • Elemental powders of a melting point depressant material generally do not provide sufficiently rapid melting.
  • Prealloyed low melting temperature powders having an alloy composition different from the base alloy composition generally produce a non-homogeneous composition and microstructure in the densified part, resulting in poor mechanical properties.
  • the low melting temperature constituent is in the form of a separate powder with particle size similar to that of the base metal powder so that the two metal powders may be blended efficiently by conventional mechanical mixing techniques, and the surface contact area between the base metal powder and the lower melting temperature powder is minimized to reduce interdiffusion and ensure effective melting at the transient liquid sintering temperature.
  • Use of a base metal powder with a coating of the lower melting temperature constituent is less effective because the larger contact area of the powder coating (as compared with discrete powder particles) allows excessive interdiffusion and dilution of the melting point lowering element prior to reaching the transient liquid sintering temperature.
  • the same vacuum furnace used for eliminating the polymer binder may be used for transient liquid sintering and densification of part 15 by controlled heat treatment. Specific heat up rates and isothermal hold times within a narrow temperature range cause transient liquid sintering of part 15 to near full density with sufficiently controlled and repeatable shrinkage to produce desired shape and dimensional tolerances for net-shape part 15.
  • the critical material constituent for this stage of the process is the lower melting temperature powder, which typically comprises the base metal alloy (about 5-15% of the total volume) with an alloying addition (such as about 3-4% boron, for example) to lower the melting point of the base alloy by approximately 300-400°C.
  • the maximum isothermal hold temperature for transient liquid sintering of part 15 is above the melting point of the lower temperature (e.g., borided) alloy but below the melting point of the base metal alloy.
  • Advantages of using a lower melting temperature alloy for liquid phase sintering include the following: (1) only about 5-15% of the total metal powder melts so that collapse of fragile elements of the part under gravity is less likely (compared to the case of liquid phase sintering of the base metal alone, where all of the powder particles are partially melted); (2) sintering occurs at approximately 200-400°C lower than the melting point of the base metal alone, which provides a superior microstructure (compared to the undesirable microstructural coarsening in unmelted base metal at the higher temperatures) and has significant economic benefits with respect to furnace equipment; and (3) resolidification (in the borided case) is by isothermal dilution of boron in the liquid (i.e., by diffusion of boron into the solid base metal powder
  • preform part 15 and green support shapes 28 may be placed on a smooth, low friction plate comprising a material such as boron nitride or machined graphite, for example.
  • a smooth, low friction plate comprising a material such as boron nitride or machined graphite, for example.
  • HIP treatment may be necessary to close residual porosity and complete chemical homogenization of the part, particularly with respect to the temperature lowering component of the alloy (e.g., boron). Elimination of residual porosity is important to improve fatigue properties of part 15. Homogenization of the boron content can improve the properties of ambient temperature ductility, toughness, and high temperature strength.
  • a final HIP treatment may be necessary to optimize final mechanical properties of part 15.
  • HIP tooling or bagging is not required because residual porosity is isolated and not surface connected (thus allowing part complexity and features, such as surface connected internal channels and cavities, that are not producible in a monolithic part by any other method); and (2) the transient liquid wets all base metal powder particles, effectively scrubbing off surface oxides and other contaminants prior to resolidification.
  • the elimination of particle surface oxides and contaminants is beneficial because their presence generally causes significant reduction of fatigue and fracture properties in directly HIP treated powders.

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  • Engineering & Computer Science (AREA)
  • Manufacturing & Machinery (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Automation & Control Theory (AREA)
  • Mechanical Engineering (AREA)
  • Powder Metallurgy (AREA)
EP96111522A 1995-09-19 1996-07-17 Préparation d'ébauches métalliques sans moule Expired - Lifetime EP0764487B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US530770 1990-05-29
US08/530,770 US5745834A (en) 1995-09-19 1995-09-19 Free form fabrication of metallic components

Publications (2)

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EP0764487A1 true EP0764487A1 (fr) 1997-03-26
EP0764487B1 EP0764487B1 (fr) 1999-12-08

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US5745834A (en) 1998-04-28
JP3660069B2 (ja) 2005-06-15
EP0764487B1 (fr) 1999-12-08
CA2178884A1 (fr) 1997-03-20
DE69605509D1 (de) 2000-01-13
CA2178884C (fr) 2007-01-16
JPH09111308A (ja) 1997-04-28

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